JPS6043901B2 - Non-heat treatment type Al-Mg alloy - Google Patents
Non-heat treatment type Al-Mg alloyInfo
- Publication number
- JPS6043901B2 JPS6043901B2 JP55073458A JP7345880A JPS6043901B2 JP S6043901 B2 JPS6043901 B2 JP S6043901B2 JP 55073458 A JP55073458 A JP 55073458A JP 7345880 A JP7345880 A JP 7345880A JP S6043901 B2 JPS6043901 B2 JP S6043901B2
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- alloy
- strength
- heat
- heat treatment
- present
- Prior art date
- Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
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Description
【発明の詳細な説明】
本発明は、優れた耐応力腐食割れ性を有し且つ塗装焼付
熱や溶接熱による強度低下を起こさないＡｌ−Ｍｇ系合
金に関するものである。DETAILED DESCRIPTION OF THE INVENTION The present invention relates to an Al-Mg alloy that has excellent stress corrosion cracking resistance and does not suffer from a decrease in strength due to paint baking heat or welding heat.
Ａｌ−Ｍｇ系合金は、Ａｌ基合金の中では強度が優れた
ものとして、一般構造材料や製罐材料等に広く使用され
ている。Al-Mg alloys have excellent strength among Al-based alloys and are widely used for general structural materials, can manufacturing materials, and the like.
ところでＡｌ−Ｍｇ系合金は非熱処理合金であ。By the way, the Al-Mg alloy is a non-heat treated alloy.
り、高い強度を得る為には冷間圧延や冷間抽伸等によつ
て加工硬化を行なわせるのが通例である。ところが加工
硬化材は、常温で長時間使用すると引張り強さ及び耐力
が低下するという欠点があり、この低下率は加工率が高
い程、またＭｇ量が多い程（即ち強度が高い程）大きく
なる傾向がある。またこの加工硬化材を母材として溶接
すると、溶接熱の影響によつて溶接部周辺（熱影響部）
の強度が低下し、加工硬化によつて付与された高強度を
維持できない。更にＡｌ−Ｍｇ系合金を飲料用キヤンエ
ンドおよびボディー材さらに自動Ｊ車ボディー材および
自動車用ホィール材等に使用するときは、冷間加工によ
る成形の後塗装焼付を行なうが、焼付時の熱影響で強度
が低下する。その為軽量化及びコスト低減を目的とした
薄肉化がむつかしく、また塗装焼付による強度低下を補
う為に冷間加工率を高めると成形性が低下する。本発明
者等は前述の様な事情に着目し、従来のＡｌ−Ｍｇ系合
金の前記諸欠点即ち１長時間使用による強度劣化、２溶
接熱による強度劣化及び３塗装焼付による強度劣化をす
べて解消すべく、添加合金元素及び配合率等について詳
細な研究を進めてきた。本発明はかかる研究の結果なさ
れたものであつて、その構成とは、Ｍｇ：２〜８％及び
Ｚｎ：０．３〜３．５％を必須成分として含み、且つ下
記Ｓｉ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔｉ、Ｖ、Ｍｏ、Ｂ１及び
Ｂより成る群から選択される１種又は２種以上の元素を
含有し、Ｓｉ：０．３〜１．０％残部がＡｌ及び不可避
不純物であるところの要旨が存在する。In order to obtain high strength, it is customary to perform work hardening by cold rolling, cold drawing, etc. However, work-hardened materials have the disadvantage that their tensile strength and yield strength decrease when used for a long time at room temperature, and this decrease rate increases as the working rate increases and the amount of Mg increases (i.e., the higher the strength). Tend. Additionally, when this work-hardened material is welded as a base material, the area around the welded area (heat-affected zone) due to the influence of welding heat
The strength of the steel decreases, and the high strength imparted by work hardening cannot be maintained. Furthermore, when Al-Mg alloys are used for beverage can ends and body materials, J-car body materials, automobile wheel materials, etc., paint baking is performed after forming by cold working, but due to the heat effect during baking. Strength decreases. Therefore, it is difficult to reduce the wall thickness for the purpose of reducing weight and cost, and if the cold working rate is increased to compensate for the decrease in strength due to paint baking, the formability decreases. The present inventors focused on the above-mentioned circumstances and eliminated all of the above-mentioned drawbacks of conventional Al-Mg alloys, namely 1. strength deterioration due to long-term use, 2. strength deterioration due to welding heat, and 3. strength deterioration due to paint burning. In order to achieve this goal, detailed research has been carried out on additive alloying elements, blending ratios, etc. The present invention was made as a result of such research, and its composition includes Mg: 2 to 8% and Zn: 0.3 to 3.5% as essential components, and the following Si, Mn, Cr, Containing one or more elements selected from the group consisting of Zr, Ti, V, Mo, B1 and B, Si: 0.3 to 1.0%, the balance being Al and inevitable impurities. A gist exists.
以下添加合金元素の種類及び含有率を限定した理由につ
いて説明する。The reasons for limiting the type and content of the added alloying elements will be explained below.
Ｍｇは優れた機械的強度を付与するのに不可欠の元素で
あり、目的達成の為には２％以上含有させる必要がある
。Mg is an essential element for imparting excellent mechanical strength, and must be contained in an amount of 2% or more to achieve the purpose.
しかし多すぎると成形性が低下し、特にキヤンボデイー
材等としての適正を確保できなくなるので８％以下に止
めねばならない。Ｚｎは本発明において最も重要な元素
の１つで、長時間使用による強度低下を防止すると共に
、熱影響（溶接熱又は塗装焼付熱）による強度低下を防
止するのに不可欠の元素であり、これらの効果を有意に
発揮させる為には０．３％以上含有させねばならない。
しかしこれらの効果は３．５％程度で飽和状態に達し、
それを越える配合は無意味であるばかりでなく圧延加工
性および耐食性を劣化させるのて好ましくない。この他
本発明では選択元素としてＳｉ，Ｍｎ，Ｃｒ，Ｚｒ，Ｔ
ｉ，Ｖ，ＭＯ，Ｂｉ及びＢよりなる群から選択される１
種又は２種以上の元素が配合されるが、何れの元素を選
択するかは、以下に示す各元素の作用を考慮し用途に応
じて適当に決めればよい。However, if the amount is too high, the moldability decreases, and in particular, it becomes impossible to ensure suitability for use as a material for a vehicle body, etc., so it must be kept at 8% or less. Zn is one of the most important elements in the present invention, and is an essential element to prevent strength loss due to long-term use and also to prevent strength loss due to heat effects (welding heat or paint baking heat). In order to exhibit the effect significantly, it must be contained in an amount of 0.3% or more.
However, these effects reach saturation at around 3.5%,
A blend exceeding this range is not only meaningless, but also undesirable as it deteriorates rolling workability and corrosion resistance. In addition, in the present invention, Si, Mn, Cr, Zr, and T are selected as selected elements.
1 selected from the group consisting of i, V, MO, Bi and B
One or more elements may be blended, and which element to select may be appropriately determined depending on the intended use, taking into consideration the effects of each element shown below.
Ｓ１は溶接熱や塗装焼付熱による強度低下を防止すると
共に耐応力腐食割れ性を高める作用があり、これらの効
果は０．８％以上の配合で有意に発．揮される。S1 has the effect of preventing strength reduction due to welding heat and paint baking heat and increasing stress corrosion cracking resistance, and these effects are significant when the content is 0.8% or more. will be demonstrated.
しカルこれらの効果は１％程度で飽和状態に達し、この
量を越えると靭性を阻害するので好ましくない。Ｍｎ，
Ｃｒ，Ｚｒ，Ｔｉ，Ｖ，ＭＯ，Ｂｉ及びＢは何れも合金
の結晶組織を微細化し且つ組織を安定化して−靭性を高
める作用があり、含有率は夫々Ｍｎ：０．０５〜１．５
％、Ｃｒ：０．０５〜０．３％、Ｚｒ：０．０５〜０．
３％、Ｔｉ：０．０２〜０．２％、Ｖ：０．０１〜０．
１％、ＭＯ：０．０１〜０．２％、Ｂｉ：０．１以下、
Ｂ：０．０００１〜０．０３％の範囲から選択すべきで
ある。These effects reach a saturated state at about 1%, and exceeding this amount is undesirable because it impairs toughness. Mn,
Cr, Zr, Ti, V, MO, Bi, and B all have the effect of refining the crystal structure of the alloy, stabilizing the structure, and increasing toughness, and their content is Mn: 0.05 to 1.5.
%, Cr: 0.05-0.3%, Zr: 0.05-0.
3%, Ti: 0.02-0.2%, V: 0.01-0.
1%, MO: 0.01 to 0.2%, Bi: 0.1 or less,
B: Should be selected from the range of 0.0001 to 0.03%.
しかして上記元素の含有率が下限値未満では上記の効果
が有意に発揮されず、一方上限値を越える当りでは上記
効果が飽和し、それ以上添加しても効果の向上は殆んど
ない。このほか本発明の合金中にＦｅ，Ｓｎ等を混入す
る場合でも、Ｆｅ≦０．５％、Ｓｎ≦０．２％の程ノ度
であれば、本発明の性能には殆んど影響しない。以上の
様に本発明では、Ｎ−Ｍｇ系合金に含有させる他の合金
元素の種類及び含有率を特定することにより、公知のＡ
１−Ｍｇ系合金の特徴を留保．しつつ、その欠点とされ
ていた長時間使用による強度劣化及び熱影響（溶接熱や
塗装焼付熱）による強度劣化を大幅に改善したもので、
非熱処理材としてのＡ１−Ｍｇ系合金の実用性を高め得
た意義は頗る大きい。However, if the content of the above elements is less than the lower limit, the above effect will not be significantly exhibited, while if it exceeds the upper limit, the above effect will be saturated, and even if the content exceeds the upper limit, there will be little improvement in the effect. In addition, even if Fe, Sn, etc. are mixed into the alloy of the present invention, as long as Fe≦0.5% and Sn≦0.2%, the performance of the present invention is hardly affected. . As described above, in the present invention, the known A
1-Retains the characteristics of Mg-based alloys. However, it has greatly improved its disadvantages of strength deterioration due to long-term use and heat effects (welding heat and paint baking heat).
The significance of being able to improve the practicality of the A1-Mg alloy as a non-heat treated material is significant.
次に本発明の実施例を示す。Next, examples of the present invention will be shown.
実施例１
第１表に示す成分組成のＡｌ−Ｍｇ系合金を溶融・鋳造
した後、５００℃で８時間均質化処理し、その後４００
〜４５０℃で熱間圧延を行ない、次いで所定の加効率で
冷間圧延して３Ｔｆ＄ｔ厚の板材を得た。Example 1 After melting and casting an Al-Mg alloy having the composition shown in Table 1, it was homogenized at 500°C for 8 hours, and then homogenized at 400°C.
Hot rolling was carried out at ~450°C, and then cold rolling was carried out at a predetermined acceleration rate to obtain a plate material with a thickness of 3Tf$t.
得られた各板材の冷間圧延直後の機械的性質及び１２０
℃で７日間加熱（常温での３年間放置に相当する）した
後の機械的性質を測定した（ＪＩＳ５号試験片）。結果
を第２表に示す。また１２０℃で所定時間加熱した後の
応力腐食割れ試験を行ない、第３表の結果を得た。Mechanical properties of each plate obtained immediately after cold rolling and 120
Mechanical properties were measured after heating at ℃ for 7 days (equivalent to 3 years of standing at room temperature) (JIS No. 5 test piece). The results are shown in Table 2. Further, a stress corrosion cracking test was conducted after heating at 120° C. for a predetermined time, and the results shown in Table 3 were obtained.
厚さ３ｍｎ１幅１−、長さ１０−の試験片を長手方向か
ら採取し、曲げ半径８ｔ（ｔ：板厚）にて１８０度の曲
げを行なう。A test piece with a thickness of 3 mm, a width of 1-, and a length of 10- is taken from the longitudinal direction and bent 180 degrees at a bending radius of 8t (t: plate thickness).
その後試験片を３．５％ＮａＣｌ水溶液に浸漬し、該試
験片を陽極として４０ｎ１Ａ／Ｉｎｃｈ２の電流を流し
て割れを観察した。尚第３表において、Ｏ印及び×（α
）は下記の意味を表わしている。Ｏ印：試験時間１４０
紛後も割れが発生しない×（α）：試験時間α分間で割
れが発生第１〜３表からも明らかな様に、本発明の漏を
満足するＮ−Ｍｇ系合金は加熱による強度劣化が極めて
少なく、また応力腐食割れ性の低下も殆んどみられない
。Thereafter, the test piece was immersed in a 3.5% NaCl aqueous solution, and a current of 40 n1A/Inch2 was applied using the test piece as an anode to observe cracks. In addition, in Table 3, O mark and ×(α
) represents the following meaning. O mark: Exam time 140
No cracking occurs even after heating x (α): Cracking occurs after a test time of α minutes. The amount of stress corrosion is extremely small, and there is almost no decrease in stress corrosion cracking resistance.
これに対し比較合金（Ｚｎが含まれていない合金）では
、加熱（常温長時間の放置も含めて）による強度及び耐
応力腐食割れ性の劣化は双方極めて著しい。実施例２
第４表に示す成分組成のＡｌ−Ｍｇ系合金を溶融・鋳造
した後、５００℃で８時間均質化処理し、その後４００
〜４５０℃で熱間圧延を行ない、次いで加工率７０％で
冷間圧延して０．５ｗｍ厚の板材を得た。On the other hand, in comparison alloys (alloys that do not contain Zn), both strength and stress corrosion cracking resistance deteriorate significantly due to heating (including when left at room temperature for a long time). Example 2 After melting and casting an Al-Mg alloy having the composition shown in Table 4, it was homogenized at 500°C for 8 hours, and then homogenized at 400°C.
Hot rolling was performed at ~450°C, and then cold rolling was performed at a processing rate of 70% to obtain a plate material with a thickness of 0.5 wm.
得られた各板材の冷間加工のまま機械的性質及び２００
℃で３０分間加熱（通常の塗装焼付条件に相当する）し
た後の機械的性質を測定した（ＪＩＳ５号試験片）。結
果を第５表に示す。また各板材を下記の条件で深絞り試
験に付し、第６表の結果を得た。The mechanical properties and 200
Mechanical properties were measured after heating at ℃ for 30 minutes (corresponding to normal paint baking conditions) (JIS No. 5 test piece). The results are shown in Table 5. Further, each plate material was subjected to a deep drawing test under the following conditions, and the results shown in Table 6 were obtained.
試験板：板厚０．５
７０％冷間加工板
しわ押え荷重：５００ｋ９
ポ ン チ ：５０ＴｍＩｒＬφ平頭
第５表からも明らかな様に、従来のＮ−Ｍｇ系合金では
加熱によつて引張り強さが大幅に低下するのに対し、本
発明の要件を充足する合金は加熱しても殆んど強度低下
を起こさない。Test plate: Plate thickness 0.5, 70% cold-worked plate Wrinkle holding load: 500k9 Punch: 50TmIrLφ flat head As is clear from Table 5, the tensile strength of conventional N-Mg alloys is reduced by heating. On the other hand, alloys that meet the requirements of the present invention hardly experience any decrease in strength even when heated.
また第６表からも明らかな様に、本発明の合金は従来の
Ａ１−Ｍｇ系合金に比べ深絞り性能も良好であり、中で
も選択元素としてＳｉを配合した合金の深絞り性能は最
も優れている。Furthermore, as is clear from Table 6, the alloy of the present invention has better deep drawing performance than the conventional A1-Mg alloy, and among them, the alloy containing Si as a selective element has the best deep drawing performance. There is.
実施例３
第７表に示す成分組成のＮ−Ｍｇ系合金を、実施例１と
同様にして溶融・鋳造、均質化処理及び熱間圧延した後
、冷間圧延して厚さ６Ｔｆｒｍの板材を得た。Example 3 An N-Mg alloy having the composition shown in Table 7 was melted and cast, homogenized, and hot rolled in the same manner as in Example 1, and then cold rolled to form a plate material with a thickness of 6Tfrm. Obtained.
得られた各板材を母材とし、ＡＡ−５１８３を溶接，ワ
イヤとして、電流２５０Ａ一電圧２５Ｖ一速度５０ｃｍ
／分の溶接条件で２層溶接を行ない、熱影響部と熱影響
を受けていない部分の機械的性質を比較した。Each of the obtained plates was used as a base material, and AA-5183 was welded and wired at a current of 250 A, a voltage of 25 V, and a speed of 50 cm.
Two-layer welding was performed under welding conditions of /min, and the mechanical properties of the heat-affected zone and the non-heat-affected part were compared.
結果を第８表に示す。また合金慟．１４（実施例）及び
合金褐．１７（比較合″金：ＡＡ−５０８３）を母材と
して得た各溶接物について、溶接部からの距離と硬度の
関係を測定したところ、第１図の結果が得られた。The results are shown in Table 8. Also, alloy. 14 (Example) and alloy brown. When the relationship between the distance from the weld and the hardness was measured for each welded product obtained using No. 17 (comparative alloy: AA-5083) as the base material, the results shown in FIG. 1 were obtained.
第８表からも明らかな様に、従来のＮ−Ｍｇ系合金では
溶接熱によつて機械的強度が大幅に劣化するが、本発明
の合金は溶接熱による強度低下が少ない。As is clear from Table 8, the mechanical strength of conventional N--Mg alloys is significantly degraded by welding heat, but the alloy of the present invention exhibits little decrease in strength due to welding heat.
また第８表からも明らかな様に、従来のＮ−Ｍｇ系合金
では溶接部の硬度低下が大きく、且つ溶接部から約５−
の範囲に亘つて明らかな硬度低下がみられるが、本発明
の合金では溶接部の硬度低下が少なく、且つ硬度低下は
溶接部から約２０ＴＩｒＩｎの範囲に止まつている。こ
れらの結果からも、本発明の合金が溶接用構造材料とし
て極めて優れたものであることが明白である。In addition, as is clear from Table 8, with conventional N-Mg alloys, the hardness of the welded part decreases significantly, and about 5-
However, in the alloy of the present invention, the hardness decrease is small in the weld zone, and the decrease in hardness is limited to a range of about 20 TIrIn from the weld zone. From these results, it is clear that the alloy of the present invention is extremely excellent as a structural material for welding.
第１図は本発明合金について溶接熱の硬さ分布に及ぼす
影響を従来合金と対比して示すグラフである。FIG. 1 is a graph showing the influence of welding heat on hardness distribution for the alloy of the present invention in comparison with a conventional alloy.
Claims (1)
成分として含み、且つ下記Ｓｉ、Ｍｎ、Ｃｒ、Ｚｒ、Ｔ
ｉ及びＢより成る群から選択される１種又は２種以上の
元素を含有し、Ｓｉ：０．３〜１．０％ Ｍｎ：０．０５〜１．５％ Ｃｒ：０．０５〜０．３％ Ｚｒ：０．０５〜０．３％ Ｔｉ：０．０２〜０．２％ Ｂ：０．０００１〜０．０３％ 残部がＡｌ及び不可避不純物であることを特徴とする耐
軟化特性および耐応力腐食割れ性の優れた非熱処理型Ａ
ｌ−Ｍｇ系合金。 ２ 特許請求の範囲第１項において、少なくともＳｉ：
０．３〜１％を必須成分として含有する熱劣化の少ない
非熱処理型Ａｌ−Ｍｇ系合金。[Claims] 1 Contains Mg: 2 to 8% and Zn: 0.3 to 3.5% as essential components, and contains the following Si, Mn, Cr, Zr, T
Contains one or more elements selected from the group consisting of i and B, Si: 0.3-1.0% Mn: 0.05-1.5% Cr: 0.05-0. 3% Zr: 0.05-0.3% Ti: 0.02-0.2% B: 0.0001-0.03% The remainder is Al and inevitable impurities. Non-heat treated type A with excellent stress corrosion cracking resistance
l-Mg alloy. 2. In claim 1, at least Si:
A non-heat treatment type Al-Mg alloy containing 0.3 to 1% as an essential component and having little thermal deterioration.
Priority Applications (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP55073458A JPS6043901B2 (en) | 1980-05-31 | 1980-05-31 | Non-heat treatment type Al-Mg alloy |
Applications Claiming Priority (1)
| Application Number | Priority Date | Filing Date | Title |
|---|---|---|---|
| JP55073458A JPS6043901B2 (en) | 1980-05-31 | 1980-05-31 | Non-heat treatment type Al-Mg alloy |
Publications (2)
| Publication Number | Publication Date |
|---|---|
| JPS56169745A JPS56169745A (en) | 1981-12-26 |
| JPS6043901B2 true JPS6043901B2 (en) | 1985-10-01 |
Family
ID=13518819
Family Applications (1)
| Application Number | Title | Priority Date | Filing Date |
|---|---|---|---|
| JP55073458A Expired JPS6043901B2 (en) | 1980-05-31 | 1980-05-31 | Non-heat treatment type Al-Mg alloy |
Country Status (1)
| Country | Link |
|---|---|
| JP (1) | JPS6043901B2 (en) |
Families Citing this family (8)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS5941433A (en) * | 1982-09-02 | 1984-03-07 | Nippon Light Metal Co Ltd | Aluminum-magnesium alloy for casting |
| JPS59143040A (en) * | 1983-02-04 | 1984-08-16 | Kobe Steel Ltd | Al alloy for welded structure |
| JPS6050139A (en) * | 1983-08-27 | 1985-03-19 | Kobe Steel Ltd | Aluminum alloy having superior screw characteristic |
| JPS60125346A (en) * | 1983-12-12 | 1985-07-04 | Kobe Steel Ltd | High strength aluminum alloy having superior workability |
| EP0799900A1 (en) | 1996-04-04 | 1997-10-08 | Hoogovens Aluminium Walzprodukte GmbH | High strength aluminium-magnesium alloy material for large welded structures |
| CN103740988B (en) * | 2013-11-27 | 2016-01-20 | 余姚市吴兴铜业有限公司 | A kind of preparation method of trolley part high-performance aluminium alloy |
| CN105543589B (en) * | 2015-12-18 | 2018-04-06 | 百色学院 | A kind of aluminum alloy casting rod special for hub and preparation method thereof |
| CN105543588A (en) * | 2015-12-18 | 2016-05-04 | 百色学院 | Special aluminum alloy ingot for casting hubs and preparation method of aluminum alloy ingot |
Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS50122411A (en) * | 1974-03-14 | 1975-09-26 | ||
| US4081294A (en) * | 1974-11-26 | 1978-03-28 | Reynolds Metals Company | Avoiding type A luder lines in forming sheet made of an Al-Mg alloy |
| JPS558499A (en) * | 1978-07-05 | 1980-01-22 | Alusuisse | Production of aluminummmagnesium alloy sheet |
-
1980
- 1980-05-31 JP JP55073458A patent/JPS6043901B2/en not_active Expired
Patent Citations (3)
| Publication number | Priority date | Publication date | Assignee | Title |
|---|---|---|---|---|
| JPS50122411A (en) * | 1974-03-14 | 1975-09-26 | ||
| US4081294A (en) * | 1974-11-26 | 1978-03-28 | Reynolds Metals Company | Avoiding type A luder lines in forming sheet made of an Al-Mg alloy |
| JPS558499A (en) * | 1978-07-05 | 1980-01-22 | Alusuisse | Production of aluminummmagnesium alloy sheet |
Also Published As
| Publication number | Publication date |
|---|---|
| JPS56169745A (en) | 1981-12-26 |
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